CN105745343B - Aluminium, Al alloy clad material and its manufacturing method and the heat exchanger and its manufacturing method for using the aluminium, Al alloy clad material - Google Patents
Aluminium, Al alloy clad material and its manufacturing method and the heat exchanger and its manufacturing method for using the aluminium, Al alloy clad material Download PDFInfo
- Publication number
- CN105745343B CN105745343B CN201480062580.5A CN201480062580A CN105745343B CN 105745343 B CN105745343 B CN 105745343B CN 201480062580 A CN201480062580 A CN 201480062580A CN 105745343 B CN105745343 B CN 105745343B
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- intermediate layer
- solder
- covering
- aluminium
- core material
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- 239000000463 material Substances 0.000 title claims abstract description 344
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 137
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 69
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 66
- 239000004411 aluminium Substances 0.000 title claims abstract description 65
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 61
- 239000011162 core material Substances 0.000 claims abstract description 161
- 229910000679 solder Inorganic materials 0.000 claims abstract description 148
- 238000005476 soldering Methods 0.000 claims abstract description 91
- 238000010438 heat treatment Methods 0.000 claims abstract description 77
- 238000005096 rolling process Methods 0.000 claims abstract description 72
- 239000002245 particle Substances 0.000 claims abstract description 65
- 238000002425 crystallisation Methods 0.000 claims abstract description 63
- 230000008025 crystallization Effects 0.000 claims abstract description 63
- 239000000956 alloy Substances 0.000 claims abstract description 21
- 238000000034 method Methods 0.000 claims description 110
- 230000008569 process Effects 0.000 claims description 85
- 238000000137 annealing Methods 0.000 claims description 42
- 238000005097 cold rolling Methods 0.000 claims description 34
- 230000009467 reduction Effects 0.000 claims description 33
- 238000005098 hot rolling Methods 0.000 claims description 32
- 229910052748 manganese Inorganic materials 0.000 claims description 23
- 238000005266 casting Methods 0.000 claims description 22
- 229910052804 chromium Inorganic materials 0.000 claims description 21
- 229910052719 titanium Inorganic materials 0.000 claims description 21
- 229910052726 zirconium Inorganic materials 0.000 claims description 21
- 229910052720 vanadium Inorganic materials 0.000 claims description 20
- 229910052742 iron Inorganic materials 0.000 claims description 19
- 239000012535 impurity Substances 0.000 claims description 15
- 229910052802 copper Inorganic materials 0.000 claims description 12
- 229910052710 silicon Inorganic materials 0.000 claims description 11
- 229910052712 strontium Inorganic materials 0.000 claims description 9
- 230000004907 flux Effects 0.000 claims description 3
- 230000033228 biological regulation Effects 0.000 claims description 2
- 230000007797 corrosion Effects 0.000 abstract description 70
- 238000005260 corrosion Methods 0.000 abstract description 70
- 229910045601 alloy Inorganic materials 0.000 abstract description 18
- 239000000203 mixture Substances 0.000 abstract description 5
- 239000010410 layer Substances 0.000 description 151
- 239000013078 crystal Substances 0.000 description 39
- 230000000694 effects Effects 0.000 description 36
- 230000000052 comparative effect Effects 0.000 description 34
- 229910000765 intermetallic Inorganic materials 0.000 description 30
- 238000012545 processing Methods 0.000 description 21
- 238000005219 brazing Methods 0.000 description 18
- 239000000243 solution Substances 0.000 description 17
- 238000005728 strengthening Methods 0.000 description 17
- 239000004615 ingredient Substances 0.000 description 13
- 229910052751 metal Inorganic materials 0.000 description 12
- 239000002184 metal Substances 0.000 description 12
- 239000010405 anode material Substances 0.000 description 10
- 238000005516 engineering process Methods 0.000 description 8
- 238000011156 evaluation Methods 0.000 description 8
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 238000003466 welding Methods 0.000 description 6
- 229910018643 Mn—Si Inorganic materials 0.000 description 5
- 239000000654 additive Substances 0.000 description 4
- 230000000996 additive effect Effects 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 4
- 238000005259 measurement Methods 0.000 description 4
- 208000014451 palmoplantar keratoderma and congenital alopecia 2 Diseases 0.000 description 4
- 229910052708 sodium Inorganic materials 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 229910052725 zinc Inorganic materials 0.000 description 4
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 3
- 229910018580 Al—Zr Inorganic materials 0.000 description 3
- QQHSIRTYSFLSRM-UHFFFAOYSA-N alumanylidynechromium Chemical compound [Al].[Cr] QQHSIRTYSFLSRM-UHFFFAOYSA-N 0.000 description 3
- 238000005452 bending Methods 0.000 description 3
- 229910052737 gold Inorganic materials 0.000 description 3
- 239000010931 gold Substances 0.000 description 3
- 239000011229 interlayer Substances 0.000 description 3
- 238000011835 investigation Methods 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 239000012071 phase Substances 0.000 description 3
- 239000011347 resin Substances 0.000 description 3
- 229920005989 resin Polymers 0.000 description 3
- 229910018131 Al-Mn Inorganic materials 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 2
- 229910018461 Al—Mn Inorganic materials 0.000 description 2
- 229910018520 Al—Si Inorganic materials 0.000 description 2
- 239000002253 acid Substances 0.000 description 2
- -1 aluminium Gold Chemical compound 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000000498 cooling water Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000002050 diffraction method Methods 0.000 description 2
- 230000005611 electricity Effects 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 230000014759 maintenance of location Effects 0.000 description 2
- 238000012797 qualification Methods 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 239000003507 refrigerant Substances 0.000 description 2
- 230000002441 reversible effect Effects 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910018084 Al-Fe Inorganic materials 0.000 description 1
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018473 Al—Mn—Si Inorganic materials 0.000 description 1
- 229910018507 Al—Ni Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- 229910000952 Be alloy Inorganic materials 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000002788 crimping Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 235000013399 edible fruits Nutrition 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 230000003631 expected effect Effects 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 239000011856 silicon-based particle Substances 0.000 description 1
- 239000005413 snowmelt Substances 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D53/00—Making other particular articles
- B21D53/02—Making other particular articles heat exchangers or parts thereof, e.g. radiators, condensers fins, headers
- B21D53/04—Making other particular articles heat exchangers or parts thereof, e.g. radiators, condensers fins, headers of sheet metal
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/0008—Soldering, e.g. brazing, or unsoldering specially adapted for particular articles or work
- B23K1/0012—Brazing heat exchangers
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/19—Soldering, e.g. brazing, or unsoldering taking account of the properties of the materials to be soldered
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/04—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by means of a rolling mill
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
- B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or welding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/001—Interlayers, transition pieces for metallurgical bonding of workpieces
- B23K35/002—Interlayers, transition pieces for metallurgical bonding of workpieces at least one of the workpieces being of light metal
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0222—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in soldering, brazing
- B23K35/0233—Sheets, foils
- B23K35/0238—Sheets, foils layered
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
- B23K35/286—Al as the principal constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950 degrees C
- B23K35/286—Al as the principal constituent
- B23K35/288—Al as the principal constituent with Sn or Zn
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/016—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of aluminium or aluminium alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
- F28F21/081—Heat exchange elements made from metals or metal alloys
- F28F21/084—Heat exchange elements made from metals or metal alloys from aluminium or aluminium alloys
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F28—HEAT EXCHANGE IN GENERAL
- F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
- F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
- F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
- F28F21/089—Coatings, claddings or bonding layers made from metals or metal alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/04—Tubular or hollow articles
- B23K2101/14—Heat exchangers
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/08—Non-ferrous metals or alloys
- B23K2103/10—Aluminium or alloys thereof
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2251/00—Treating composite or clad material
Abstract
The present invention provides the aluminium, Al alloy clad material and its manufacturing method of a kind of highly corrosion resistant and high-mouldability and has used the heat exchanger and its manufacturing method of the aluminium, Al alloy clad material.Aluminium, Al alloy clad material of the invention has the core material of aluminium alloy, intermediate layer material of the covering on a surface of the core material, with solder of the covering on the surface of the non-core material side of the intermediate layer material, above-mentioned core material, intermediate layer material and solder have defined composition of alloy, crystallization particle diameter before the soldering heating of above-mentioned intermediate layer material is at 60 μm or more, on the section along rolling direction of the above-mentioned core material before soldering heating, the crystallization particle diameter in plate thickness direction is set as R1 (μm), when the crystallization particle diameter of rolling direction is set as R2 (μm), R1/R2 is below 0.30.
Description
Technical field
The present invention relates to the aluminium, Al alloy clad materials and its manufacturing method of highly corrosion resistant and high-mouldability, specifically,
It is resistance to be related to being suitable as the height that the access constituent material of refrigerant or high temperature compressed air in the heat exchangers such as radiator uses
The aluminium, Al alloy clad material and its manufacturing method of corrosivity and high-mouldability.The invention further relates to use above-mentioned highly corrosion resistant and
The heat exchanger of the aluminium, Al alloy clad material of high-mouldability, particularly the channel-forming member for being related to automobile heat exchanger etc.,
And its manufacturing method.
Background technique
Aluminium alloy light weight and have high thermal conductivity, highly corrosion resistant can be realized by processing appropriate, therefore, answered
For automobile heat exchanger, such as radiator, condenser, evaporator, heater, intercooler etc..As automobile heat exchange
The tubing of device is used and is closed by core material, single side top covering Al-Si system's aluminium in side of the Al-Mn such as 3003 alloys line aluminium alloy
2 layers of clad material obtained from the solder of gold or the sacrificial anode material of Al-Zn line aluminium alloy；Or in these 2 layers of covering materials
In material, 3 layers of clad material obtained from the solder of further covering Al-Si line aluminium alloy on another single side of core material.Heat
Exchanger is usually by combining the tubing of such clad material with the fin material after ripple forming, with 600 DEG C or so
High temperature is brazed to make.
In the novel heat exchanger used in the recent automobile, in order to realize further high performance, tube shape
Complication upgrading.Therefore, further high-mouldability is required for material.All the time, it carries out in cold rolling
The H14 that way carries out intermediate annealing is quenched, or the H24 of progress final annealing is quenched after cold rolling, adjusts the mouldability of tubing.But
It is only quenched to be difficult to meet the requirement to high-mouldability in recent years with such.
In addition, if the surface inside and outside the pipe of the heat exchanger, which exists, has corrosive liquid, it is possible to due to occurring
Pitting and cause pipe to penetrate through, or cause the plate thickness of pipe to reduce due to homogeneous corrosion, compressive resistance reduces, tubing ruptures.
As a result, there is the risk that the internal air recycled or cooling water, refrigerant are revealed.Also, needing pipe and fin
Each other in the case where engagement etc., surface needs to have solder for engagement, pipe.All the time, such as in the pipe as condenser
In the case that outer surface is exposed to the harsh corrosive environment such as snow melt salt like that and needs to engage pipe with fin, by
The outer surface top covering of tubing has the layer of sacrificial anode effect as middle layer and on the outside covering solder, Neng Goushi
Existing corrosion resistance and soldering property and deposit.However, corrosive liquids is in particular portion sometimes due to the complication of above-mentioned tube shape
It point thickens, the only covering middle layer as the prior art is difficult to fully prevent from revealing sometimes.
The technology for improving these mouldabilities and corrosion resistance individually is proposed in the prior art.For example, about
Make the mouldability of clad material or technology that connecing property of electric seam welding improves, it is on the books in patent document 1,2.However, in these patents
In document, means that the corrosion resistance not on the books for making sacrificial anode material improves.On the other hand, about making clad material
The technology that corrosion resistance improves, it is on the books in patent document 3.However, not recording makes clad material in the patent document
Mouldability improve means.
Specifically, clad material documented by patent document 1, by by the section rectangular with length direction of core material
On average crystallite particle diameter be set as 30 μm hereinafter, improving the connecing property of electric seam welding of material.However, about sacrificial anode material, it will
0.2 μm of partial size or more of Mg2The area ratio of Si is limited to 0.5% hereinafter, but this is also the hand for improving connecing property of electric seam welding
Section.About the corrosion resistance of sacrificial anode material, the additive amount of Zn and Mg are only defined, it is existing for corrosion resistance to be increased to
Horizontal technology more than technology do not have any disclosure also there is no suggestion that.
In addition, clad material documented by patent document 2 makes the electricity seam of material by making core material form bacillar structure
Weldability improves.However, about sacrificial anode material, it is specified that the hardness of core material and sacrificial anode material is 50Hv or more and hard
The ratio between degree (sacrificial anode material/core material) is lower than 1.0, but this is for ensuring that the means of the fatigue strength after soldering heating.It closes
In the corrosion resistance of sacrificial anode material, the additive amount of Zn and Mn are also merely specified here, for corrosion resistance to be increased to
For the horizontal technology more than prior art, without any disclosure also there is no suggestion that.
On the other hand, in the clad material documented by patent document 3, by the way that the crystallization particle diameter of sacrificial anode material is set
It is 100~700 μm, improves the corrosion resistance under alkaline environment.However, ingredient is only defined for core material, for its tissue
Do not recorded with engineering properties etc., any disclosure no for the raising of mouldability also there is no suggestion that.
Also, the equal covering of sacrificial anode material documented by these patent documents is on the surface of the material, do not record about
Technology between core material and solder as middle layer setting.
Existing technical literature
Patent document
Patent document 1: Japanese Unexamined Patent Publication 8-291354 bulletin
Patent document 2: Japanese Unexamined Patent Publication 2010-255014 bulletin
Patent document 3: Japanese Unexamined Patent Publication 11-209837 bulletin
Summary of the invention
Subject to be solved by the invention
The present invention was completed to solve the above problem, and its purpose is to provide a kind of by aluminium, Al alloy clad material example
Such as the tubing of heat exchanger in use, with excellent mouldability and be brazed heating after intermediate layer material have it is excellent
Corrosion resistance aluminium, Al alloy clad material and its manufacturing method and using the aluminium, Al alloy clad material heat exchanger and its
Manufacturing method.The aluminium, Al alloy clad material of such highly corrosion resistant and high-mouldability is suitable as the stream of automobile heat exchanger
Road forming member uses.
Means for solving the problems
The present inventor has made intensive studies the above subject, as a result, it has been found that distinguishing covering as clad material
The material of core material and intermediate layer material with specific composition of alloy and metal structure is able to solve the above subject, thus complete
At the present invention.
That is, the item 1 of the 1st aspect of the present invention is a kind of aluminium, Al alloy clad material, it is characterised in that: have aluminium alloy
The surface of intermediate layer material on a surface of the core material of core material, covering and covering in the non-core material side of the intermediate layer material
On solder, above-mentioned core material is made of aluminium alloy, and the aluminium alloy for constituting above-mentioned core material contains Si:0.05~1.50mass%, Fe:
0.05~2.00mass%, Mn:0.5~2.0mass%, remainder include Al and inevitable impurity；Above-mentioned middle layer
Material is made of aluminium alloy, constitute above-mentioned intermediate layer material aluminium alloy contain Zn:0.5~8.0mass%, Si:0.05~
1.50mass%, Fe:0.05~2.00mass%, remainder include Al and inevitable impurity；Above-mentioned solder is closed by aluminium
Gold is constituted, and the aluminium alloy for constituting above-mentioned solder contains Si:2.5~13.0mass%, Fe:0.05~1.20mass%, remainder
Subpackage contains Al and inevitable impurity；Crystallization particle diameter before the soldering heating of above-mentioned intermediate layer material is at 60 μm or more, in pricker
On the section along rolling direction of above-mentioned core material before weldering heating, the crystallization particle diameter in plate thickness direction is set as R1 (μm), rolling
When the crystallization particle diameter in direction is set as R2 (μm), R1/R2 is below 0.30.
Item 2 of the invention is that above-mentioned core material is by also containing selected from Mg:0.05~0.50mass%, Cu:0.05 in item 1
~1.50mass%, Ti:0.05~0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:
One kind or two or more aluminium alloy in 0.05~0.30mass% is constituted.
Item 3 of the invention is, in item 1 or 2, above-mentioned intermediate layer material by also containing selected from Ni:0.05~
2.00mass%, Mn:0.05~2.00mass%, Ti:0.05~0.30mass%, Zr:0.05~0.30mass%, Cr:
One kind or two or more aluminium alloy in 0.05~0.30mass% and V:0.05~0.30mass% is constituted.
Item 4 of the invention is, in any one of item 1~3, above-mentioned solder by also containing selected from Zn:0.5~
8.0mass%, Cu:0.05~1.50mass%, Mn:0.05~2.00mass%, Ti:0.05~0.30mass%, Zr:0.05
One kind or two or more aluminium alloy in~0.30mass%, Cr:0.05~0.30mass% and V:0.05~0.30mass%
It constitutes.
Item 5 of the invention is, in any one of item 1~4, above-mentioned solder by also containing selected from Na:0.001~
1 kind or 2 kinds of aluminium alloy in 0.050mass% and Sr:0.001~0.050mass% is constituted.
Item 6 of the invention is a kind of manufacturing method of aluminium, Al alloy clad material, is used to manufacture any one of item 1~5 institute
The aluminium, Al alloy clad material stated, above-mentioned manufacturing method are characterised by comprising: cast respectively above-mentioned core material aluminium alloy, in
The process of the aluminium alloy of the aluminium alloy and solder of interlayer material；The intermediate layer material ingot bar and solder ingot bar that casting is obtained
It is hot-rolled down to the hot-rolled process of specific thickness respectively；The middle layer of specific thickness has been made in a surface top covering of core material ingot bar
Material, the surface top covering in the non-core material side of the intermediate layer material have been made the solder of specific thickness, clad material are made
Covering process；The covering hot-rolled process of hot rolling is carried out to clad material；Cold rolling is carried out to the clad material Jing Guo covering hot rolling
Cold rolling process；With anneal when one of after the midway of cold rolling process and cold rolling process or both to clad material 1
The secondary above annealing operation, in above-mentioned covering hot-rolled process, rolling start temperature is 400~520 DEG C, by the temperature of clad material
Degree is that the reduction ratio of 200~400 DEG C of 1 passages of period is limited in 5 times in 30% or more rolling pass hereinafter, in above-mentioned lehr attendant
In sequence, clad material is kept for 1~10 hour with 200~560 DEG C.
The item 7 of the 2nd aspect of the present invention is a kind of aluminium, Al alloy clad material, it is characterised in that: has the core of aluminium alloy
Material, covering on a surface of the core material intermediate layer material, covering is on the surface of the non-core material side of the intermediate layer material
Solder on another surface of the core material of solder and covering, above-mentioned core material is made of aluminium alloy, constitutes above-mentioned core material
Aluminium alloy contains Si:0.05~1.50mass%, Fe:0.05~2.00mass%, Mn:0.5~2.0mass%, remainder
Comprising Al and inevitable impurity, above-mentioned intermediate layer material is made of aluminium alloy, constitutes the aluminium alloy of above-mentioned intermediate layer material
Containing Zn:0.5~8.0mass%, Si:0.05~1.50mass%, Fe:0.05~2.00mass%, remainder includes Al
With inevitable impurity, solder and covering of the covering on the surface of the non-core material side of above-mentioned intermediate layer material are in above-mentioned core material
Another surface on solder be made of aluminium alloy, the aluminium alloy for constituting solder contains Si:2.5~13.0mass%, Fe:
0.05~1.20mass%, remainder includes Al and inevitable impurity, before the soldering heating of above-mentioned intermediate layer material
Crystallization particle diameter is at 60 μm or more, on the section along rolling direction of the above-mentioned core material before soldering heating, by plate thickness direction
When crystallization particle diameter is set as R1 (μm), the crystallization particle diameter of rolling direction is set as R2 (μm), R1/R2 is below 0.30.
Item 8 of the invention is, in item 7, above-mentioned core material is by also containing selected from Mg:0.05~0.50mass%, Cu:0.05
~1.50mass%, Ti:0.05~0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:
One kind or two or more aluminium alloy in 0.05~0.30mass% is constituted.
Item 9 of the invention is, in item 7 or 8, above-mentioned intermediate layer material by also containing selected from Ni:0.05~
2.00mass%, Mn:0.05~2.00mass%, Ti:0.05~0.30mass%, Zr:0.05~0.30mass%, Cr:
One kind or two or more aluminium alloy in 0.05~0.30mass% and V:0.05~0.30mass% is constituted.
Item 10 of the invention is, in any one of item 7~9, table of the covering in the non-core material side of above-mentioned intermediate layer material
The solder of solder and covering on another surface of above-mentioned core material on face by also containing selected from Zn:0.5~8.0mass%,
Cu:0.05~1.50mass%, Mn:0.05~2.00mass%, Ti:0.05~0.30mass%, Zr:0.05~
One kind or two or more aluminium alloy structure in 0.30mass%, Cr:0.05~0.30mass% and V:0.05~0.30mass%
At.
Item 11 of the invention is, in any one of item 7~10, table of the covering in the non-core material side of above-mentioned intermediate layer material
The solder of solder and covering on another surface of above-mentioned core material on face by also containing selected from Na:0.001~
1 kind or 2 kinds of aluminium alloy in 0.050mass% and Sr:0.001~0.050mass% is constituted.
Item 12 of the invention is a kind of manufacturing method of aluminium, Al alloy clad material, is used to manufacture any one of item 7~11
The aluminium, Al alloy clad material, the manufacturing method are characterised by comprising: cast respectively above-mentioned core material aluminium alloy, in
The aluminium alloy and covering of solder of the aluminium alloy, covering of interlayer material on the surface of the non-core material side of intermediate layer material exist
The process of the aluminium alloy of solder on another surface of core material；Obtained intermediate layer material ingot bar, covering will be cast in centre
The solder ingot bar of solder ingot bar and covering on another surface of core material on the surface of the non-core material side of layer material is warm respectively
It is rolled to the hot-rolled process of specific thickness；The intermediate layer material of specific thickness has been made in a surface top covering of core material ingot bar,
The solder of specific thickness has been made in surface top covering in the non-core material side of the intermediate layer material, in another table of core material ingot bar
The solder of specific thickness has been made in face top covering, and the covering process of clad material is made；The covering of hot rolling is carried out to clad material
Hot-rolled process；The cold rolling process of cold rolling is carried out to the clad material Jing Guo covering hot rolling；With in the midway of cold rolling process and cold rolling
1 time or more the annealing operation annealed when one of after process or both to clad material, in above-mentioned covering Hot-roller
In sequence, rolling start temperature is 400~520 DEG C, and the reduction ratio that the temperature of clad material is 200~400 DEG C of 1 passages of period is existed
30% or more rolling pass is limited in 5 times hereinafter, in above-mentioned annealing operation, and clad material keeps 1 with 200~560 DEG C~
10 hours.
Item 13 of the invention is a kind of heat exchanger, to use aluminium alloy described in any one of item 1~5 and 7~11
The heat exchanger of clad material, it is characterised in that: soldering heating after the intermediate layer material crystallization particle diameter 100 μm with
On.
Item 14 of the invention is a kind of manufacturing method of heat exchanger, is used to manufacture heat exchanger described in item 13, should
Manufacturing method is characterized in that, in inactive gas atmosphere, is brazed using solder flux to aluminum alloy materials.
Invention effect
Aluminium, Al alloy clad material of the invention for example in the tubing as heat exchanger in use, even if pipe it is complex-shaped
Also it can form well, and after soldering heating, excellent corrosion resistance is shown due to intermediate layer material.It will in this way
Aluminium, Al alloy clad material be applied to channel-forming member etc., be capable of providing the heat exchanger of automobile etc..From acid etch resistance etc.
From the perspective of the also excellent and light weight of soldering property and good heat conductivity, which is suitable as the heat of automobile
Exchanger tubing.
Detailed description of the invention
Fig. 1 is the schematic diagram for indicating the crystal grain surrounded on the rolling surface of intermediate layer material by crystal boundary.
Fig. 2 is the crystallization particle diameter R1 and rolling direction in the plate thickness direction on the section along rolling direction for indicate core material
The schematic diagram of crystallization particle diameter R2.
Fig. 3 is the inclined of the section along rolling direction when carrying out anodized to the core material with bacillar structure
Light microscope photo.
Specific embodiment
To the aluminium, Al alloy clad material and its manufacturing method for having both highly corrosion resistant and high-mouldability of the invention and make
It is described in detail with the preferred embodiment of the heat exchanger of the aluminium, Al alloy clad material and its manufacturing method.
1. constituting the layer of aluminium, Al alloy clad material
Aluminium, Al alloy clad material of the invention, by the ingredient and metal structure of suitable control core material, have it is excellent at
Type；Also, the ingredient and metal structure for passing through intermediate layer material of the suitable control covering on a surface of core material, have
Excellent corrosion resistance.In the aluminium, Al alloy clad material of the 1st aspect of the present invention, for the packet on another surface of core material
Layer is without especially system limit.For example, in the case where pipe is by the methods of welding tubulation and does not need with fin brazed, this hair
The aluminium, Al alloy clad material of bright first method, can also be with what not covering on another surface of core material.And it is carrying out
In the case where the soldering of soldering between tubing or pipe and fin, the aluminium alloy packet as the 2nd aspect of the present invention
Layer material, also covering has solder on another surface of core material.
In the following, for above-mentioned core material, intermediate layer material and two kinds of solder, that is, coverings in the non-core material side of intermediate layer material
Surface on solder on another surface of core material of solder (hereinafter referred to as " the first solder ") and covering (hereinafter referred to as
" the second solder ") ingredient be illustrated.2. core material
The core material of first method and second method is used (to be simply denoted as below containing Si:0.05~1.50mass%
" % "), Fe:0.05~2.00%, Mn:0.5~2.0% as must element, remainder include Al and inevitably it is miscellaneous
The aluminium alloy of matter.
Also, in addition to containing other than above-mentioned necessary element in the core material of two ways, can also containing selected from Mg:0.05~
0.50%, Cu:0.05~1.50%, Ti:0.05~0.30%, Zr:0.05~0.30%, Cr:0.05~0.30% and V:
The addition element of one kind or two or more alternatively property in 0.05~0.30%.
The core material of two ways can also contain and divide other than the addition element containing above-mentioned necessary element and selectivity
Not below 0.05%, integrally in 0.15% inevitable impurity below.
Aluminium alloy used in the core material of two ways is suitble to be alloy, such as 3003 alloy of JIS etc. using JIS 3000
Al-Mn system alloy.Each ingredient is described in detail below, these each ingredients are same in first method and second method
's.
Si:
Si and Fe, Mn be formed together the intermetallic compound of Al-Fe-Mn-Si system, passes through the dispersion-strengthened core material that makes
Intensity improves, or is dissolved in aluminium parent phase, improves the intensity of core material by solution strengthening.Si content be 0.05~
1.50%.When lower than 0.05%, it is necessary to use raffinal parent metal, cost increases.And when more than 1.50%, core material
A possibility that fusing point reduces, and core material melts when soldering is increased.Si content is preferably 0.10~1.20%.
Fe:
Fe and Si, Mn be formed together the intermetallic compound of Al-Fe-Mn-Si system, passes through the dispersion-strengthened core material that makes
Intensity improves.The additive amount of Fe is 0.05~2.00%.When content is lower than 0.05%, it is necessary to raffinal parent metal is used,
Cost increases.And when more than 2.00%, when casting huge intermetallic compound easy to form, make plastic processing reduction.Fe
Content is preferably 0.10~1.50%.
Mn:
Mn and Si is formed together the intermetallic compound of Al-Mn-Si system or Al-Fe-Mn-Si system, strong by dispersing
Change improves the intensity of core material, or is dissolved in aluminium parent phase, improves the intensity of core material by solution strengthening.Mn content is
0.5~2.0%.When lower than 0.5%, said effect is unsatisfactory, when more than 2.0%, when casting huge gold easy to form
Compound between category makes plastic processing reduction.Mn content is preferably 0.8~1.8%.
Mg:
Mg passes through Mg2The precipitation of Si and improve the intensity of core material, it is possible to contain.Mg content be 0.05~
0.50%.When lower than 0.05%, said effect is unsatisfactory, and when more than 0.50%, soldering is difficult.Mg content is preferably
0.10~0.40%.
Cu:
Cu improves the intensity of core material by solution strengthening, it is possible to contain.Cu content is 0.05~1.50%.It is lower than
When 0.05%, said effect is unsatisfactory, and when more than 1.50%, a possibility that aluminium alloy ruptures when casting increases.
Cu content is preferably 0.30~1.00%.Ti:
Ti improves the intensity of core material by solution strengthening, it is possible to contain.Ti content is 0.05~0.30%.It is lower than
When 0.05%, said effect is unsatisfactory.When more than 0.30%, huge intermetallic compound easy to form adds plasticity
Work reduces.Ti content is preferably 0.10~0.20.
Zr:
Zr improves the intensity of core material by solution strengthening, and have the intermetallic compound of Al-Zr system is precipitated,
The effect of coarse grains after heating soldering, it is possible to contain.Zr content is 0.05~0.30%.Lower than 0.05%
When, said effect can not be obtained.And when more than 0.30%, huge intermetallic compound easy to form makes plastic processing reduction.
Zr content is preferably 0.10~0.20%.
Cr:
Cr improves the intensity of core material by solution strengthening, and have the intermetallic compound of Al-Cr system is precipitated,
The effect of coarse grains after heating soldering, it is possible to contain.Cr content is 0.05~0.30%.Lower than 0.05%
When, said effect can not be obtained.And when more than 0.30%, huge intermetallic compound easy to form makes plastic processing reduction.
Cr content is preferably 0.10~0.20%.
V:
V improves the intensity of core material by solution strengthening, and also improves corrosion resistance, it is possible to contain.V content
It is 0.05~0.30%.When lower than 0.05%, said effect can not be obtained.And when more than 0.30%, huge metal easy to form
Between compound, make plastic processing reduction.V content is preferably 0.10~0.20%.
These Mg, Cu, Ti, Zr, Cr and V are as needed containing at least one kind of in core material.
3. intermediate layer material
The intermediate layer material of first method and second method use containing Zn:0.5~8.0%, Si:0.05~1.50%,
Fe:0.05~2.00% is as necessary element, aluminium alloy of the remainder comprising Al and inevitable impurity.
Also, the intermediate layer material of two ways, can also be containing selected from Ni other than containing above-mentioned necessary element:
0.05~2.00%, Mn:0.05~2.00%, Ti:0.05~0.30%, Zr:0.05~0.30%, Cr:0.05~0.30%
With the addition element of the one kind or two or more alternatively property in V:0.05~0.30%.Also, in two ways, in addition to containing
Have except above-mentioned necessary element and the addition element of selectivity, it can also be containing each comfortable 0.05% or less, entirety 0.15%
Inevitable impurity below.Each ingredient is illustrated below, these each ingredients are in first method and second method
Similarly.
Zn:
Zn can reduce Pitting Potential, by forming the potential difference with core material, can be made using sacrifice anticorrosion ability resistance to
Corrosivity improves.The content of Zn is 0.5~8.0%.When lower than 0.5%, it cannot sufficiently be utilized and sacrifice anticorrosion ability
Improve the effect of corrosion resistance.And when more than 8.0%, corrosion rate is accelerated, and intermediate layer material disappears in advance, corrosion resistance drop
It is low.Zn content is preferably 1.0~6.0%.
Si:
Si and Fe are formed together the intermetallic compound of Al-Fe-Si system, and when containing Mn at the same time and Fe, Mn mono-
The intermetallic compound for forming Al-Fe-Mn-Si system is acted, is improved by the dispersion-strengthened intensity for making intermediate layer material, or
It is dissolved in aluminium parent phase, improves the intensity of intermediate layer material by solution strengthening.In addition, Si mentions the current potential of intermediate layer material
Height, thus inhibit to sacrifice anticorrosion ability, reduce corrosion resistance.The content of Si is 0.05~1.50%.Content is lower than
When 0.05%, it is necessary to use raffinal parent metal, cost increases.And when more than 1.50%, the pitting of intermediate layer material
Current potential is got higher, and is lost and is sacrificed anticorrosion ability, and corrosion resistance reduces.Si content is preferably 0.10~1.20%.
Fe:
Fe and Si are formed together the intermetallic compound of Al-Fe-Si system, and when containing Mn at the same time and Si, Mn mono-
The intermetallic compound for forming Al-Fe-Mn-Si system is acted, is improved by the dispersion-strengthened intensity for making intermediate layer material.Fe's
Additive amount is 0.05~2.00%.When content is lower than 0.05%, it is necessary to use raffinal parent metal, cost increases.And
When more than 2.00%, when casting huge intermetallic compound easy to form, make plastic processing reduction.Fe content is preferably 0.10
~1.50%.
Ni:
Ni forms Al-Ni system or the intermetallic compound that Al-Fe-Ni system is formed together with Fe.Between these metals
Compound is since corrosion potential is much higher than aluminum matrix, so playing the effect in the cathode site as corrosion.Therefore, if these
Intermetallic compound disperses in intermediate layer material, and the starting point of corrosion just will disperse.As a result, the corrosion to depth direction be difficult into
Row, corrosion resistance improves, therefore can contain.Also, Ni also has the effect of making the intensity of intermediate layer material to improve.Therefore,
In order to improve corrosion resistance and intensity, the content of Ni is 0.05~2.00%.When lower than 0.05%, cannot fully it obtain
State the effect that corrosion resistance and intensity improve.And when more than 2.00%, when casting huge intermetallic compound easy to form, make
Plastic processing reduces.Ni content is preferably 0.10~1.50%.
Mn:
Mn improves the intensity of intermediate layer material and corrosion resistance, it is possible to contain.The content of Mn be 0.05~
2.00%.When more than 2.00%, when casting huge intermetallic compound easy to form, make plastic processing reduction.And it is being lower than
When 0.05%, its effect cannot be fully obtained.Mn content is preferably 0.05~1.80%.
Ti:
Ti improves the intensity of intermediate layer material by solution strengthening, and improves corrosion resistance also, it is possible to contain
Have.Ti content is 0.05~0.30%.When lower than 0.05%, said effect can not be obtained.It is easy to form huge when more than 0.30%
Big intermetallic compound makes plastic processing reduction.Ti content is preferably 0.05~0.20%.
Zr:
Zr improves the intensity of intermediate layer material by solution strengthening, and has the intermetallic compound for making Al-Zr system
The effect of coarse grains after being precipitated, heating soldering, it is possible to contain.Zr content is 0.05~0.30%.It is lower than
When 0.05%, said effect can not be obtained.And when more than 0.30%, huge intermetallic compound easy to form adds plasticity
Work reduces.Zr content is preferably 0.10~0.20%.
Cr:
Cr improves the intensity of intermediate layer material by solution strengthening, and has the intermetallic compound for making Al-Cr system
The effect of coarse grains after being precipitated, heating soldering, it is possible to contain.Cr content is 0.05~0.30%.It is lower than
When 0.05%, said effect can not be obtained.When more than 0.30%, huge intermetallic compound easy to form makes plastic processing
It reduces.Cr content is preferably 0.10~0.20%.
V:
V improves the intensity of intermediate layer material by solution strengthening, and also improves corrosion resistance, it is possible to contain
Have.V content is 0.05~0.30%.When lower than 0.05%, said effect can not be obtained.It is easy to form huge when more than 0.30%
Big intermetallic compound makes plastic processing reduction.V content is preferably 0.05~0.20%.
These Ni, Mn, Ti, Zr, Cr and V are as needed containing at least one kind of in intermediate layer material.
4. solder
The first solder and the second solder in first method and second method, which use, contains Si:2.5~13.0%, Fe:
0.05~1.20% as necessary element, aluminium alloy of the remainder comprising Al and inevitable impurity.
In addition, the solder of two ways is other than above-mentioned necessary element, can also containing selected from Zn:0.5~8.0%,
Cu:0.05~1.50%, Mn:0.05~2.00%, Ti:0.05~0.30%, Zr:0.05~0.30%, Cr:0.05~
0.30% and V:0.05~0.30% in the one kind or two or more addition element as first choice.Also, in addition to above-mentioned
It, can also be containing selected from Na except necessary element or other than above-mentioned necessary element and the addition element of first choice:
0.001~0.050% and Sr:0.001~0.050% in a kind or 2 kinds as second selectivity addition element.Also,
In two ways, in addition to the addition of the addition element containing above-mentioned necessary element and first choice and/or the second selectivity
Except element, it can also contain respectively below 0.05%, integrally in 0.15% inevitable impurity below.Below to each
Ingredient is illustrated, these each ingredients are same in first method and second method.Si:
By adding Si, the fusing point of solder is reduced, and generates liquid phase, to make it possible to be brazed.Si content be 2.5~
13.0%.When lower than 2.5%, the liquid phase of generation is few, and soldering is difficult to function.And when more than 13.0%, such as inciting somebody to action
In the case that the solder is used for tubing, the Si amount spread to subject materials such as fins is excessive, the melting of generating object material.Si contains
Amount preferably 3.5~12.0%.
Fe:
The intermetallic compound of Fe Al-Fe system easy to form or Al-Fe-Si system, thus make for being brazed effective Si
Amount reduces, and leads to the reduction of soldering property.Fe content is 0.05~1.20%.When lower than 0.05%, it is necessary to use high-purity aluminium base
Body metal leads to high cost.And when more than 1.20%, make to reduce for being brazed effective Si amount, be brazed insufficient.Fe content
Preferably 0.10~0.50%.
Zn:
Zn can reduce Pitting Potential, by forming the potential difference with core material, can be made using sacrifice anticorrosion ability resistance to
Corrosivity improves, it is possible to contain.The content of Zn is 0.5~8.0%.When lower than 0.5%, cannot fully it obtain using sacrificial
The effect of domestic animal anticorrosion ability raising corrosion resistance.And when more than 8.0%, corrosion rate is accelerated, and sacrifices corrosion-resistant coating and shifts to an earlier date
It disappears, corrosion resistance reduces.Zn content is preferably 1.0~6.0%.
Cu:
Cu improves the intensity of solder by solution strengthening, it is possible to contain.Cu content is 0.05~1.50%.Low
When 0.05%, said effect is insufficient；A possibility that aluminium alloy rupture occurs when more than 1.50%, when casting increases.Cu
Content is preferably 0.30~1.00%.Wherein, in the case where solder is free of Zn, the preferred content of Cu is 0.05~0.60%.
Since Cu can be improved Pitting Potential, so sacrificing anticorrosion ability by Zn bring sometimes can lose when more than 0.6%.
Mn:
Mn can be such that the intensity of solder and corrosion resistance improves, it is possible to contain.The content of Mn is 0.05~2.00%.
When more than 2.00%, when casting huge intermetallic compound easy to form, make plastic processing reduction.And it is being lower than 0.05%
When, it cannot fully obtain its effect.Mn content is preferably 0.05~1.80%.
Ti:
Ti, which improves solution strengthening, improves the intensity of solder, and improves corrosion resistance also, it is possible to contain.Ti contains
Amount is 0.05~0.30%.When lower than 0.05%, said effect can not be obtained.When more than 0.30%, huge metal easy to form
Between compound, make plastic processing reduction.Ti content is preferably 0.10~0.20%.
Zr:
Zr improves the intensity of solder by solution strengthening, and have the intermetallic compound of Al-Zr system is precipitated,
The effect of coarse grains after heating soldering, it is possible to contain.Zr content is 0.05~0.30%.Lower than 0.05%
When, said effect can not be obtained.When more than 0.30%, huge intermetallic compound easy to form makes plastic processing reduction.Zr
Content is preferably 0.10~0.20%.
Cr:
Cr improves the intensity of solder by solution strengthening, and have the intermetallic compound of Al-Cr system is precipitated,
The effect of coarse grains after heating soldering, it is possible to contain.Cr content is 0.05~0.30%.Lower than 0.05%
When, said effect can not be obtained.When more than 0.30%, huge intermetallic compound easy to form makes plastic processing reduction.Cr
Content is preferably 0.10~0.20%.
V:
V improves the intensity of solder by solution strengthening, and also improves corrosion resistance, it is possible to contain.V content
It is 0.05~0.30%.When lower than 0.05%, said effect can not be obtained.When more than 0.30%, between huge metal easy to form
Compound makes plastic processing reduction.V content is preferably 0.10~0.20%.
Na, Sr:
Na, Sr play the effect for making the Si Particle pollution in solder.The content of Na, Sr is respectively 0.001~
0.050%.When respective content is lower than 0.001%, said effect cannot be fully obtained.And it is more than in respective content
When 0.050%, oxide film thereon thickens, and reduces soldering property.Respective preferred content is 0.003~0.020%.
These Zn, Cu, Mn, Ti, Zr, Cr, V, Na and Sr are as needed containing at least one kind of in solder.
5. the crystallization particle diameter of intermediate layer material
In aluminium, Al alloy clad material of the invention, the crystallization particle diameter of the intermediate layer material before soldering heating is limited to 60
μm or more, the crystallization particle diameter of intermediate layer material after soldering heating be limited to 100 μm or more.This be in order to realize soldering heating after
The raising of the corrosion resistance of intermediate layer material.Wherein, as shown in Figure 1, crystallization particle diameter here refers among from rolling surface
Layer material, will be by crystal boundary area encompassed as crystal grain, the arithmetic mean of instantaneous value of the equivalent circle diameter of the crystal grain.In addition, so-called
Crystal boundary refers to that adjacent crystalline orientation difference is 20 degree or more of boundary.The measuring method of crystallization particle diameter is not particularly limited, generally
Utilize electron beam back scattering diffraction method (EBSD).Illustrate its restriction reason below.
Intermediate layer material is preferentially corroded for the purpose of sacrificing anticorrosion and by covering by making it, make corrosion with planar into
Row, prevents the pitting corrosion of pipe.But if the corrosion rate of the intermediate layer material is fast, intermediate layer material will disappear ahead of time
It loses, loses and sacrifice etch-proof effect, pitting corrosion will occur for pipe.
The inventor of invention passes through further investigation, as a result, it has been found that, the etch ratio of the crystal grain boundary in intermediate layer material
It is fast in crystal grain, by reducing the area of crystal grain boundary, it is able to suppress corrosion rate.Make what the area of the crystal grain boundary reduced to contain
Justice is equal to increase crystallization particle diameter.By studying in more detail, if having distinguished the knot of the intermediate layer material after soldering heating
Crystal size is 100 μm or more, then the corrosion rate of intermediate layer material is suppressed, and aluminium, Al alloy clad material has excellent corrosion resistant
Corrosion.In the case that the crystallization particle diameter of intermediate layer material is lower than 100 μm after soldering heating, due to the corrosion speed of intermediate layer material
Degree is fast, sacrifices anticorrosion ability and loses in advance, so being unable to get effective corrosion resistance.Also, the centre after soldering heating
The crystallization particle diameter of layer material is preferably 120 μm or more.In addition, the upper limit value of the crystallization particle diameter of the intermediate layer material after soldering heating
It is not particularly limited, but is difficult to be set as 1000 μm or more.
The present inventor is further studied, as a result, it has been found that, the knot of the intermediate layer material before soldering heating
The crystallization particle diameter of intermediate layer material after crystal size and soldering heating has positively related relationship.That is, soldering heating in order to obtain
The crystallization particle diameter of the big crystallization particle diameter of intermediate layer material afterwards, the intermediate layer material before needing to be brazed heating increases.For this
It is a little studied in detail, situation of the crystallization particle diameter of the intermediate layer material before as a result having distinguished soldering heating at 60 μm or more
Under, the crystallization particle diameter of the intermediate layer material after soldering heating will reach 100 μm or more.It is brazed the intermediate layer material before heating
In the case that crystallization particle diameter is lower than 60 μm, the crystallization particle diameter of the intermediate layer material after soldering heating will be lower than 100 μm.In addition,
The crystallization particle diameter of intermediate layer material before soldering heating is preferably 80 μm or more.In addition, the intermediate layer material being brazed before heating
The upper limit value of crystallization particle diameter is not particularly limited, but is difficult to be set as 1000 μm or more.
6. the crystallization particle diameter of core material
Aluminium, Al alloy clad material of the invention is on the section along rolling direction of the core material before soldering heating, by plate thickness
When the crystallization particle diameter in direction is set as R1 (μm), the crystallization particle diameter of rolling direction is set as R2 (μm), by R1/R2 be defined as 0.30 with
Under.This is the index for improving the mouldability of the clad material before soldering is heated.As shown in Fig. 2, crystallization particle diameter R1 here
Refer to R2 (μm), observes the section along rolling direction of clad material, it, will be each using the region surrounded by crystal boundary as crystal grain
The maximum gauge in the plate thickness direction of crystal grain is defined as R1, and the maximum gauge of rolling direction is defined as R2.In addition, so-called crystal boundary is
Refer to that adjacent crystalline orientation difference is 20 degree or more of boundary.The measuring method of crystallization particle diameter is not particularly limited, general to utilize electricity
Beamlet back scattering diffraction method (EBSD).In addition, carrying out anode after mirror ultrafinish in the very big situation of degree of finish of core material
Oxidation, when with polarized light microscope observing anodic oxidation face, it can be observed that bacillar structure as shown in Figure 3.In such feelings
Under condition, the crystallization particle diameter in plate thickness direction is completely collapsed, and is defined as R1=0.
As described above, the mouldability of aluminium alloy passes through using being determined by the condition or rolling rate later of intermediate annealing
It is quenched and adjust engineering properties to improve.However, material occurs broken when implementing the process of bending machining under stringent condition etc.
It splits.Further investigation is repeated in the present inventor, as a result, it has been found that the crystal grain of the core material before soldering heating is along rolling side
To section on it is more flat in the rolling direction, more can obtain excellent mouldability.Then, in the present invention, with above-mentioned R1/
Index of the R2 as the flatness for indicating crystal grain.The detailed research of inventor through the invention has distinguished that in R1/R2 be 0.30
When following, the crystal grain of core material becomes very flat, has excellent mouldability.If R1/R2 is more than 0.30, the crystal grain of core material
Flatness it is inadequate, can not have excellent processability.R1/R2 is preferably 0.20 or less.Here, R1/R2 is smaller, and flatness is got over
Greatly, processability is better, thus preferably.In addition, as described above, R1=0, R1/R2 are 0 can also be with.
7. the manufacturing method of aluminium, Al alloy clad material
The mode of 7-1. manufacturing method
The manufacturing method of the aluminium, Al alloy clad material of above-mentioned first method of the invention includes: the aluminium for casting core material respectively
The process of the aluminium alloy of alloy, the aluminium alloy of intermediate layer material and the first solder；The intermediate layer material casting that casting is obtained
Block and the first solder ingot bar are hot-rolled down to the hot-rolled process of specific thickness respectively；It has been made in a surface top covering of core material ingot bar
The intermediate layer material of specific thickness, the first solder of specific thickness has been made in covering on the other surface, and clad material is made
Covering process；The covering hot-rolled process of hot rolling is carried out to clad material；Cold rolling is carried out to the clad material Jing Guo covering hot rolling
Cold rolling process；With anneal to clad material when one of after the midway of cold rolling process and cold rolling process or both
1 time or more annealing operation.
The manufacturing method of the aluminium, Al alloy clad material of above-mentioned second method of the invention includes: the aluminium for casting core material respectively
Alloy, the aluminium alloy of intermediate layer material, the aluminium alloy of the first solder and the second solder aluminium alloy process；It will casting
Obtained intermediate layer material ingot bar, the first solder ingot bar and the second solder ingot bar are hot-rolled down to the hot-rolled process of specific thickness respectively；
The intermediate layer material of specific thickness is made in a surface top covering of core material ingot bar, in the non-core material side of the intermediate layer material
Surface top covering the first solder of specific thickness has been made, regulation has been made in another surface top covering of the core material ingot bar
The covering process of clad material is made in second solder of thickness；The covering hot-rolled process of hot rolling is carried out to clad material；To process
The clad material of covering hot rolling carries out the cold rolling process of cold rolling；With one of after the midway of cold rolling process and cold rolling process or
1 time or more the annealing operation annealed when the two to clad material.
7-2. casting process and hot-rolled process
Condition in the casting process of core material, the first solder and the second solder and intermediate layer material is not particularly limited,
Usually carried out by water-cooled semi-continuous casting.In addition, dividing by core material, intermediate layer material, the first solder and the second solder
It is not hot-rolled down in the process of specific thickness, heating condition is preferably to be carried out 1~10 hour with 400~560 DEG C of temperature.It is lower than
At 400 DEG C, plastic processing shortcoming, therefore edge break etc. is generated sometimes in rolling.In the high temperature more than 560 DEG C,
It may cause the ingot bar in heating to melt.When heating time is lower than 1 hour, the non-uniform temperature of ingot bar, plastic processing shortcoming,
Edge break etc. is generated sometimes in rolling, when more than 10 hours, hence it is evident that damage productivity.
7-3. covering hot-rolled process
In the manufacturing method of the aluminium, Al alloy clad material of above-mentioned first and second mode, in covering hot-rolled process, rolling
Start temperature is 400~520 DEG C, is 30% or more by the reduction ratio that the temperature of clad material is 200~400 DEG C of 1 passages of period
Rolling pass be limited to 5 times or less.In addition, covering hot-rolled process can be divided into thick rolling process and smart rolling process.Finish rolling
In process processed, the roll mill of reversible or the roll mill of tandem type are used.In reversible roll mill, 1 rolling of single track is determined
Justice is 1 passage, and in tandem type roll mill, the rolling using 1 group of Rolling roller is defined as 1 passage.
Firstly, being illustrated to rolling pass.As described above, aluminium, Al alloy clad material of the invention needs to heat in soldering
Before in the state of increase intermediate layer material crystallization particle diameter.The crystal grain of intermediate layer material is formed in annealing operation during manufacturing
, the strain accumulated before annealing to intermediate layer material is bigger, and the driving force of the grain growth generated in annealing is bigger, just
It can obtain bigger crystal grain.On the other hand, make in the state that aluminium, Al alloy clad material of the invention is needed before soldering heating
The crystal grain of core material is flat state.The crystal grain of core material is also in forming in the annealing operation in manufacture, the core before annealing
The strain accumulated in material is smaller, and the driving force for the grain growth to plate thickness direction that when annealing generates is with regard to smaller, result energy
Access more flat crystal grain.
That is, increasing the crystal grain of intermediate layer material and the crystal grain of core material being made to become flat in the relationship violated.Therefore, with existing
There is technology to be difficult to take into account the two.But further investigation is repeated in the present inventor, as a result, it has been found that passing through covering hot rolling
The control of process, which can be realized, to be taken into account.
When temperature when covering hot rolling is lower temperature, if carrying out the big rolling pass of reduction ratio, biggish shearing
Strain is easily accessible the central portion of material.Specifically, in covering hot-rolled process, by the temperature of clad material be 200~
The rolling pass that reduction ratio is 30% or more during 400 DEG C is limited in 5 situations below, into the shear strain in core material
It is few, in the state of before soldering heating, the crystal grain of core material can be made to become flat.Due in covering hot-rolled process, covering material
During the temperature of material is more than 400 DEG C, dynamic recovery occurs in covering hot rolling, so, even if implementing reduction ratio is 30% or more
Rolling pass, due to enter core material in shear strain do not increase, so not influencing the flatness of core material crystal grain.Another party
Face when the temperature of the clad material in covering hot-rolled process is lower than 200 DEG C, generates rupture, can not manufacture clad material in hot rolling.
In addition, in the case that the reduction ratio of 1 passage is lower than 30%, since the shear strain entered in core material does not increase, so not influencing
The flatness of core material crystal grain.The rolling pass that reduction ratio is 30% or more during the temperature of clad material is 200~400 DEG C is preferred
Below 4 passages.In addition, above-mentioned reduction ratio is preferably 35% or more.In addition, if application is more than 50% rolling pass, material
Rupture etc. may occur for material.
On the other hand, in covering hot-rolled process, even if reduction ratio during being 200~400 DEG C by the temperature of clad material
Rolling pass for 30% or more is limited to 5 times hereinafter, also generating big in intermediate layer material near the surface layer of clad material
Shear strain.Therefore, sufficient grain growth occurs in intermediate layer material in intermediate annealing, can be obtained in intermediate layer material
To big crystal grain.That is, the crystallization particle diameter of intermediate layer material can be made to become thick by the above-mentioned control in covering hot rolling, and
And the crystal grain of core material is made to become flat.
Then, illustrate to roll start temperature.The crystallization particle diameter of intermediate layer material before soldering heating can be wrapped by adjusting
Rolling start temperature in layer hot-rolled process controls.The start temperature of covering hot rolling is if it is 520 DEG C hereinafter, then in covering heat
Big shear strain is generated when rolling in intermediate layer material, the crystallization particle diameter of the intermediate layer material before being capable of increasing soldering heating.
In the case that the start temperature of covering hot rolling is more than 520 DEG C, when covering hot rolling, generates dynamic recovery in intermediate layer material, shears
Strain is reduced, the crystallization particle diameter of the intermediate layer material before can not increasing soldering heating.And the material temperature when covering hot rolling starts
When degree is lower than 400 DEG C, material breaks are generated in rolling.Therefore, the start temperature of covering hot rolling is set as 400~520 DEG C.Its
In, the start temperature of covering hot rolling is preferably 420~500 DEG C.
In addition, the reduction ratio during the temperature of clad material is 200~400 DEG C in covering hot-rolled process is 30% or more
Road number is without being especially arranged lower limit.However, not including the case where in 1 passage of passage that reduction ratio is 30% or more yet
Under, expected effect, needs to increase the passage that reduction ratio is lower than 30%, therefore damage productivity in order to obtain.It is therefore preferable that packet
Include the passage that the reduction ratio of 1 passage or more is 30% or more.In addition, preferably with 400~560 DEG C to covering before covering hot rolling
Material heats 1~10 hour.When heating temperature is lower than 400 DEG C, material temperature when due to rolling is too low, may send out in rolling
Green material rupture.And if heating temperature is more than 560 DEG C, solder may melt.In addition, when heating time was less than 1 hour, material
Material temperature degree is difficult to uniformly.And when heated between more than 10 hours when, sometimes obviously damage productivity.In addition, after covering hot rolling
Plate thickness be not particularly limited, it is usually preferred to be set as 2.0~5.0mm or so.
7-4. annealing operation
In the manufacturing process of the aluminium, Al alloy clad material of above-mentioned first method and second method, cold rolling process midway and
Setting carries out 1 annealing operation annealed above to clad material in one of after cold rolling process or both.Specifically, being
Refer to: (1) implementing the process of 1 time or more intermediate annealing in the midway of cold rolling process, (2) implement 1 time most after cold rolling process
(1) and (2) is implemented in whole annealing operation, or (3).In the annealing operation, clad material is kept 1~10 with 200~560 DEG C
Hour.
Annealing operation is carried out for the purpose of adjusting the strain in material, but can make intermediate layer material again by the process
Crystallization obtains big crystal grain as described above.The case where clad material temperature in annealing operation is lower than 200 DEG C or guarantor
Hold the time it is small less than 1 in the case of, recrystallizing for intermediate layer material is not over.The case where annealing temperature is more than 560 DEG C
Under, solder is possible to generate melting.In addition, the retention time, even more than 10 hours, also there is no problem for the performance of clad material, but
Obvious damage productivity.
In addition, the upper limit of the number of annealing operation is not particularly limited, but in order to avoid the increase bring because of process number
Increased costs, preferably 3 times or less.
7-5. homogenize process process
Can by ingot bar obtained from cast aluminium alloy gold core material before covering process for homogenize process process.Homogeneous
Change treatment process generally preferably to keep ingot bar 1~20 hour with 450~620 DEG C.The case where temperature is lower than 450 DEG C or guarantor
In the case where the time is held less than 1 time, homogenizing effect be may be insufficient, if it exceeds 620 DEG C, it is likely that generate core material
The melting of ingot bar.In addition, the retention time, even more than 20 hours, homogenizing effect is also saturated, lack economy.
7-6. covering rate
In aluminium, Al alloy clad material of the invention, the covering rate (single side) of preferred interlayer material is 3~25%.As above
It is described, in the covering hot-rolled process in manufacturing process, need only to apply intermediate layer material big shear strain.However, such as
The covering rate of fruit intermediate layer material is more than 25%, then cannot integrally apply sufficient shear strain to intermediate layer material, sometimes not
It can make intermediate layer material that recrystallized structure be integrally formed.And the covering rate of intermediate layer material be lower than 3% when, due to intermediate layer material
It is excessively thin, so cannot integrally cover intermediate layer material throughout core material sometimes in covering hot rolling.The covering rate of intermediate layer material
More preferably 5~20%.
Wherein, the covering rate of the first solder and the second solder is not particularly limited, usually with 3~30% or so coverings.
8. heat exchanger
Above-mentioned aluminium, Al alloy clad material is suitable as the heat exchanger component of tubing, tube plate (header plate) etc.
It uses, is used particularly suitable as tubing.For example, implementing brake forming to above-mentioned aluminium, Al alloy clad material, by its both ends
Intersection soldered joint makes the tubing for media such as the cooling waters that circulates.In addition, being carried out to above-mentioned aluminium, Al alloy clad material
Processing makes the tube plate with hole engaged with the both ends of tubing.Heat exchanger of the invention is for example with will be above-mentioned
Tubing, fin material and tube plate combination, by structure obtained from their primary soldering processing.
It is carried out in heat exchanger obtained from the soldered joint of usual conditions using such material of the invention, as above
It is described, which is characterized in that the crystallization particle diameter of the intermediate layer material of the aluminium, Al alloy clad material after soldering heating is 100 μm or more.
Feature in this way, as described above, can be realized the raising of the corrosion resistance of the intermediate layer material after soldering heating.
Above-mentioned heat exchanger is assembled in the outer surface configuration fin material that both ends are partly installed in the tubing of tube plate.
Then, both ends intersection, fin material and the pipe outer surface of tubing, the both ends of tubing and tube plate are passed through into 1 soldering
Heating simultaneously engages with.As the method for soldering, Nocolok method for brazing, vacuum brazing process, fluxless method for brazing can be used, it is excellent
Select Nocolok method for brazing.Soldering is usually by heating 2~10 minutes, preferably with 590~610 DEG C with 590~610 DEG C of temperature
Temperature heat 2~6 minutes and carry out.It is usually cooling with 20~500 DEG C/min of cooling velocity after soldering.
Embodiment
Then, based on example of the present invention and comparative example, the present invention will be described in further detail, but the present invention is not limited to
These examples.
The core alloy with composition of alloy shown in table 1 is cast by DC casting respectively, there is composition of alloy shown in table 2
Intermediate layer material alloy, solder alloy with composition of alloy shown in table 3, surface cutting is carried out to two sides respectively and is finally added
Work.Ingot bar thickness after surface cutting is 400mm.For solder and intermediate layer material, calculates final plate thickness and be that target is thick
The covering rate of degree, for heating 3 hours heating processes with 520 DEG C, to reach thickness when required combination, it
Afterwards, hot rolling is carried out until reaching specific thickness.In addition, indicating the homogenize process condition of core material in table 4.
[table 1]
[table 2]
[table 3]
Using these alloys, on a surface of core alloy the intermediate layer material of combination table 2, in intermediate layer material
The solder of combination table 3 on the surface of non-core material side.Part sample also solder of combination table 3 on another surface of core material.Its
In, solder of the covering on the surface of the non-core material side of middle layer is known as the first solder, by covering core material another table
Solder on face is known as the second solder.The covering rate of first solder and the second solder and intermediate layer material is 10%.
By these combined materials for heating process after, implement covering hot-rolled process, production 3 layers or 4 layers of 3.5mm thickness
Clad material.Temperature and time in heating process, the start temperature in covering hot-rolled process and final temperature are shown in table 4.
In addition, the temperature of clad material is 30% or more in the reduction ratio of 200 DEG C~400 DEG C 1 passages of period in covering hot-rolled process
Rolling pass implement for 1 time or more, which is shown in table 4.Wherein, in example of the present invention, any example is opened
Beginning temperature can clearly have the temperature of clad material in 400 DEG C or more, final temperature at 200 DEG C more than and less than 400 DEG C
Spend the passage at 200 DEG C~400 DEG C.After covering hot-rolled process, cold rolling is implemented to clad material.For aliquot, cold
Intermittent intermediate annealing (1 time or 2 times) is implemented in the midway rolled, and then, implements final cold rolling, makes the packet of final plate thickness 0.3mm
Layer material sample.For aliquot, without intermediate annealing, but 1 intermittent final annealing is carried out after final cold rolling,
Make the clad material sample of final plate thickness 0.3mm.Also, to other aliquot, these intermediate annealings and final are carried out
Both annealing, makes the clad material sample of final plate thickness 0.3mm.Also, the cold rolling rate after intermediate annealing is 30%.Will in
Between the condition annealed be shown in table 4.Wherein, as shown in table 4, in E14~16, intermediate annealing and final annealing are not carried out, and E16 is not
Carry out covering hot rolling.
In the case where not going wrong in above manufacturing process, the final plate thickness of 0.3mm can be rolled down to, it will manufacture
Property is evaluated as "○"；Rupture is generated in casting or when rolling and fails the final plate thickness for being rolled down to 0.3mm, in covering hot-rolled process
The crimping for generating melting in preceding heating process or intermediate annealing process or occurring in covering hot rolling is bad, can not manufacture packet
In the case where layer material, manufacturing is evaluated as "×".As a result it is shown in table 5~7.In addition, the core material in each clad material closes
The combination of gold, intermediate layer material alloy, solder alloy is also depicted in table 5~7.
Above-mentioned clad material sample is respectively evaluated obtained result and be equally shown in table 5~7 for following.Wherein, right
The case where manufacturing in table 6,7 is "×", since sample can not be manufactured, so not can be carried out following evaluations.
(evaluation of mouldability)
Cut out JIS5 test film on the direction parallel with rolling direction from each clad material sample, with rolling direction
After parallel direction carries out 5% stretching, with intermediate layer material face for curved inside, 180 ° of radius of curvature R 0.05mm are carried out
Bending.Resin embedding is carried out in a manner of it can observe bending R section, and carries out mirror ultrafinish, is commented using optical microscopy
Whether valence ruptures.As a result, core material is had occurred not there is a situation where rupturing to be evaluated as mouldability qualification (zero) for core material
It is unqualified (×) that the case where rupture, is evaluated as mouldability.It is not being evaluated in addition, rupture whether occurs in two solders, intermediate layer material
In object.
(evaluation of soldering property)
Preparing thickness 0.07mm, quenched H14, alloying component is the fin material that 1.0%Zn is added in 3003 alloys,
Heat-exchanger fin material is made in its ripple forming.The fin material is configured into the first solder in above-mentioned clad material sample
Face or the second solder face, are impregnated in 5% fluoride flux aqueous solution, for 600 DEG C, soldering heating in 3 minutes, pass through
Nocolok soldering production minicore sample.After brazing, fin is removed, according to the contact number (mountain number) of fin and solder and
The ratio for forming the position of filleting finds out fin rate of engagement.By the fin rate of engagement of the minicore sample 95% or more and
There is a situation where melt to be evaluated as soldering property qualification (zero) for clad material sample and fin.And it is lower than in (1) fin rate of engagement
In the case that 95% the case where, (2) clad material sample and fin at least either melt, (1) and (2) or (1) or
(2) it is evaluated as soldering property unqualified (×).
(measurement of the tensile strength after soldering heating)
The clad material sample of the heat treatment (being equivalent to soldering heating) of 600 DEG C, 3 minutes will be implemented in tensile speed
10mm/ minutes, under conditions of gauge length 50mm, carry out tension test according to JISZ2241.It is bent by the stress-strain obtained
Line reads tensile strength.As a result, the situation that tensile strength is 120MPa or more is evaluated as qualified (zero), the numerical value will be less than
The case where be evaluated as unqualified (×).
(measurement of the crystallization particle diameter of intermediate layer material)
To the clad material sample and pricker before soldering heating (600 DEG C, heat treatment in 3 minutes are equivalent to soldering heating)
Clad material sample after weldering heating is ground from surface, removes solder, later, is carried out to the face L-LT of intermediate layer material
Intermediate layer material particle size determination sample is made in mirror ultrafinish.By the region of 2mm × 2mm in the sample in SEM (sweep type
Electron microscope) in carry out EBSD, according to its result detect boundary that crystalline orientation difference is 20 degree or more as crystal boundary, calculating
Crystallization particle diameter (equivalent circle diameter).Wherein, at measurement site arbitrarily selected 10, use its arithmetic mean of instantaneous value as crystallization particle diameter.Separately
Outside, for due to intermediate layer material recrystallize be not over and in bacillar structure, the sample of crystallization particle diameter can not be measured
It is denoted as " threadiness ".
(measurement of the crystallization particle diameter of core material)
Using before soldering heating (600 DEG C, heat treatment in 3 minutes are equivalent to soldering heating) clad material sample and
Clad material sample after soldering heating, carries out resin embedding by the section along rolling direction in the way of aspect of measure, goes forward side by side
Core material particle size determination sample is made in row mirror ultrafinish.By the region length 2mm × thickness 0.2mm in the sample in SEM
EBSD is carried out, the boundary for being 20 degree or more according to its result detection crystalline orientation difference is as crystal boundary.Measure the plate thickness direction of crystal grain
Maximum gauge R1 and rolling direction maximum gauge R2, calculate the value of R1/R2.Wherein, crystal grain is arbitrarily surveyed in the same visual field
At fixed 10, use its arithmetic mean of instantaneous value as R1/R2.In addition, in the case where crystal grain boundary is not detected in EBSD, to mirror surface
Sample after grinding carries out anodic oxidation, with polarized light microscope observing, the case where observing bacillar structure as shown in Figure 3
Under, it is set as R1=0.
(corrosion resistance)
Using minicore sample same as sample used in the evaluation of soldering property, by the side not engaged with fin
Surface is sheltered with insulating resin, using the face engaged with fin as test face, based on JIS-H8502 for 500 hours and 1000
The CASS test of hour.As a result, the sample that clad material at 1000 hours does not generate corrosion perforation is evaluated as the resistance to of CASS
Corrosivity is outstanding qualified (◎), and the sample that clad material at 500 hours does not generate corrosion perforation is evaluated as the corrosion-resistant of CASS
Property qualified (zero), produced when by 500 hours corrosion perforation sample be evaluated as CASS corrosion resistance it is unqualified (×).Its
In, in this evaluation, all evaluation objects of the first solder, will only be added to Zn in the second solder is object.In addition, not wrapping
In the sample of the second solder of layer, (core material exposes non-covering about the core material another side of one side surface of the first solder
Face), not as evaluation object.Also, the sample for being evaluated as "×" of soldering property cannot make suitable minicore sample, not make
For evaluation object.
In example 1~12,38~45 of the present invention, meet condition given to this invention, manufacturing, soldering property, mouldability, pricker
The tensile strength and corrosion resistance of postwelding are qualified.
In contrast, in comparative example 13, since the Si content of core material is excessive, so the soldering of the first solder does not conform to
Lattice.
In comparative example 14, since the Mg content of core material is excessive, so the soldering of the first solder is unqualified.
In comparative example 15, since the Fe content of core material is excessive, so generating rupture when rolling, solder brazing can not be made
Plate, manufacturing are unqualified.
In comparative example 16, since the content of Ti, Zr, Cr and V of core material are excessive, so rupture is generated when rolling, it can not
Brazing sheet is made, manufacturing is unqualified.
In comparative example 17, since the Mn content of core material is excessive, so generating rupture when rolling, solder brazing can not be made
Plate, manufacturing are unqualified.
In comparative example 18, since the Cu content of core material is excessive, so generating rupture when casting, solder brazing can not be made
Plate, manufacturing are unqualified.
In comparative example 19, since the Mn content of core material is very few, so the tensile strength after soldering heating is unqualified.
In comparative example 20, since the Si content of intermediate layer material is excessive, so the soldering of the first solder is unqualified.
In comparative example 21, since the Fe content of intermediate layer material is excessive, so generating rupture when rolling, it can not make hard
Brazing sheet, manufacturing are unqualified.
In comparative example 22, since the content of Ti, Zr, Cr and V of intermediate layer material are excessive, so being generated when rolling broken
It splits, brazing sheet can not be made, manufacturing is unqualified.
In comparative example 23, since the Zn content of intermediate layer material is very few, so the corrosion resistance of the first solder is unqualified.
In comparative example 24, since the Zn content of intermediate layer material is excessive, so the corrosion resistance of the first solder is unqualified.
In comparative example 25, since the Ni content of intermediate layer material is excessive, so generating rupture when rolling, it can not make hard
Brazing sheet, manufacturing are unqualified.
In comparative example 26, since the Mn content of intermediate layer material is excessive, so generating rupture when rolling, it can not make hard
Brazing sheet, manufacturing are unqualified.
In comparative example 27, since the Si content of the first solder is very few, so the soldering of the first solder is unqualified.
In comparative example 28, since the Si content of the first solder is excessive, so the soldering of the first solder is unqualified.
In comparative example 29, since the Fe content of the first solder is excessive, so the soldering of the first solder is unqualified.
In comparative example 30, since the Cu content of the first solder is excessive, so generating rupture when casting, hard pricker can not be made
Welding plate, manufacturing are unqualified.
In comparative example 31, since the Mn content of the first solder is excessive, so generating rupture when rolling, hard pricker can not be made
Welding plate, manufacturing are unqualified.
In comparative example 32, since the content of Ti, Zr, Cr and V of the first solder are excessive, so rupture is generated when rolling,
Brazing sheet can not be made, manufacturing is unqualified.
In comparative example 33, since the Na content of solder is excessive, so the soldering of the first solder is unqualified.
In comparative example 34, since the Sr content of solder is excessive, so the soldering of the first solder is unqualified.
In comparative example 35, since the Zn ingredient of solder is very few, so the corrosion resistance of the second solder is unqualified.
In comparative example 36, since the Zn ingredient of solder is excessive, so the corrosion resistance of the second solder is unqualified.
In comparative example 37, since the Cu ingredient of solder is excessive, so the corrosion resistance of the second solder is unqualified.
In comparative example 46 and 47, the temperature of clad material is in 200~400 DEG C of 1 passages of period in covering hot-rolled process
The road number that reduction ratio is 30% or more is more than 5 passages.Therefore, the R1/R2 ratio of core material crystal grain is more than 0.3 before being brazed, mouldability
It is unqualified.
In comparative example 48, the start temperature of covering hot-rolled process is more than 520 DEG C.Therefore, the intermediate layer material before soldering
Crystallization particle diameter be lower than 60 μm, the crystallization particle diameter of the intermediate layer material after soldering is lower than 100 μm, and the corrosion resistance of the first solder is not
It is qualified.
In comparative example 49, the temperature of intermediate annealing is lower than 200 DEG C.Therefore, the intermediate layer material before soldering is in threadiness
The crystallization particle diameter of tissue, the intermediate layer material after soldering is lower than 100 μm, and the corrosion resistance of the first solder is unqualified.
In comparative example 50, since the temperature of intermediate annealing is more than 560 DEG C, so the first solder generates melting, no legal system
Make brazing sheet, manufacturing is unqualified.
In comparative example 51, the time of intermediate annealing was less than 1 hour.Therefore, the intermediate layer material before soldering is in threadiness
The crystallization particle diameter of tissue, the intermediate layer material after soldering is lower than 100 μm, and the corrosion resistance of the first solder is unqualified.
In comparative example 52, the heating temperature of intermediate layer material and the first solder is too low, and hot rolling sandwich rolling process
Start temperature be lower than 400 DEG C (also not including annealing operation).Therefore, rupture is generated in covering hot-rolled process, fails to make
The brazing sheet of purpose plate thickness.
In comparative example 53, the heating time of intermediate layer material and the first solder is too short, and hot rolling sandwich rolling process
Start temperature be lower than 400 DEG C (also not including annealing operation).Therefore, rupture is generated in covering hot-rolled process, fails to make
The brazing sheet of purpose plate thickness.
In comparative example 54, since the heating temperature of intermediate layer material and the first solder is excessively high, so hot rolling starts preceding temperature
Height is spent, the first solder generates melting, fails the brazing sheet for making purpose plate thickness.
Industrial availability
Aluminium, Al alloy clad material of the invention, since the intensity after soldering is high, the soldering property such as fin rate of engagement, acid etch resistance
It is also excellent with corrosion resistance, so the channel-forming member particularly suitable as automobile heat exchanger uses.
Symbol description
R1: along the crystallization particle diameter in the plate thickness direction on the core material section of rolling direction
R2: along the crystallization particle diameter of the rolling direction on the core material section of rolling direction
Claims (14)
1. a kind of aluminium, Al alloy clad material, it is characterised in that:
Have the intermediate layer material and covering of the core material, covering of aluminium alloy on a surface of the core material in the intermediate layer material
Non- core material side surface on solder,
The core material is made of aluminium alloy, and the aluminium alloy for constituting the core material contains Si:0.05~1.50mass%, Fe:0.05
~2.00mass%, Mn:0.5~2.0mass%, remainder are made of Al and inevitable impurity,
The intermediate layer material is made of aluminium alloy, constitute the intermediate layer material aluminium alloy contain Zn:0.5~
8.0mass%, Si:0.05~1.50mass%, Fe:0.05~2.00mass%, remainder by Al and inevitably it is miscellaneous
Texture at,
The solder is made of aluminium alloy, constitute the solder aluminium alloy contain Si:2.5~13.0mass%, Fe:0.05~
1.20mass%, remainder are made of Al and inevitable impurity,
The intermediate layer material soldering heating before crystallization particle diameter at 60 μm or more,
Soldering heating before the core material the section along rolling direction on, by the crystallization particle diameter in plate thickness direction be set as R1,
When the crystallization particle diameter of rolling direction is set as R2, R1/R2 is below 0.30, wherein the unit of R1 and R2 be μm,
The crystallization particle diameter of the intermediate layer material after soldering heating is at 100 μm or more.
2. aluminium, Al alloy clad material as described in claim 1, it is characterised in that:
The core material by also containing selected from Mg:0.05~0.50mass%, Cu:0.05~1.50mass%, Ti:0.05~
1 kind in 0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:0.05~0.30mass%
Or aluminium alloy of more than two kinds is constituted.
3. aluminium, Al alloy clad material as claimed in claim 1 or 2, it is characterised in that:
The intermediate layer material is by also containing selected from Ni:0.05~2.00mass%, Mn:0.05~2.00mass%, Ti:0.05
1 in~0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:0.05~0.30mass%
Kind or aluminium alloy of more than two kinds are constituted.
4. aluminium, Al alloy clad material as claimed in claim 1 or 2, it is characterised in that:
The solder by also containing selected from Zn:0.5~8.0mass%, Cu:0.05~1.50mass%, Mn:0.05~
2.00mass%, Ti:0.05~0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:
One kind or two or more aluminium alloy in 0.05~0.30mass% is constituted.
5. aluminium, Al alloy clad material as claimed in claim 1 or 2, it is characterised in that:
The solder by also containing a kind in Na:0.001~0.050mass% and Sr:0.001~0.050mass% or
2 kinds of aluminium alloy is constituted.
6. a kind of manufacturing method of aluminium, Al alloy clad material, is used for aluminium alloy described in any one of manufacturing claims 1~5
Clad material, the manufacturing method are characterised by comprising:
The process of the aluminium alloy of the aluminium alloy of the core material, the aluminium alloy of intermediate layer material and solder is cast respectively；
Intermediate layer material ingot bar and solder ingot bar that casting obtains are hot-rolled down to the hot-rolled process of specific thickness respectively；
The intermediate layer material of specific thickness is made in a surface top covering of core material ingot bar, in the non-core of the intermediate layer material
The solder of specific thickness has been made in the surface top covering of material side, and the covering process of clad material is made；
The covering hot-rolled process of hot rolling is carried out to clad material；
The cold rolling process of cold rolling is carried out to the clad material Jing Guo covering hot rolling；With
When one of after the midway of cold rolling process and cold rolling process or both, anneal to clad material 1 time or more
Annealing operation,
In the covering hot-rolled process, rolling start temperature is 400~520 DEG C, is 200~400 by the temperature of clad material
The reduction ratio of DEG C 1 passage of period be limited in 5 times in 30% or more rolling pass hereinafter,
In the annealing operation, clad material is kept for 1~10 hour with 200~560 DEG C.
7. a kind of aluminium, Al alloy clad material, it is characterised in that:
Have intermediate layer material on a surface of the core material of the core material, covering of aluminium alloy, covering in the intermediate layer material
Non- core material side surface on solder on another surface of the core material of solder and covering,
The core material is made of aluminium alloy, and the aluminium alloy for constituting the core material contains Si:0.05~1.50mass%, Fe:0.05
~2.00mass%, Mn:0.5~2.0mass%, remainder are made of Al and inevitable impurity,
The intermediate layer material is made of aluminium alloy, constitute the intermediate layer material aluminium alloy contain Zn:0.5~
8.0mass%, Si:0.05~1.50mass%, Fe:0.05~2.00mass%, remainder by Al and inevitably it is miscellaneous
Texture at,
Solder and covering of the covering on the surface of the non-core material side of the intermediate layer material are on another surface of the core material
On solder be made of aluminium alloy, constitute solder aluminium alloy contain Si:2.5~13.0mass%, Fe:0.05~
1.20mass%, remainder are made of Al and inevitable impurity,
The intermediate layer material soldering heating before crystallization particle diameter at 60 μm or more,
Soldering heating before the core material the section along rolling direction on, by the crystallization particle diameter in plate thickness direction be set as R1,
When the crystallization particle diameter of rolling direction is set as R2, R1/R2 is below 0.30, wherein the unit of R1 and R2 be μm,
The crystallization particle diameter of the intermediate layer material after soldering heating is at 100 μm or more.
8. aluminium, Al alloy clad material as claimed in claim 7, it is characterised in that:
The core material by also containing selected from Mg:0.05~0.50mass%, Cu:0.05~1.50mass%, Ti:0.05~
1 kind in 0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:0.05~0.30mass%
Or aluminium alloy of more than two kinds is constituted.
9. aluminium, Al alloy clad material as claimed in claim 7 or 8, it is characterised in that:
The intermediate layer material is by also containing selected from Ni:0.05~2.00mass%, Mn:0.05~2.00mass%, Ti:0.05
1 in~0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:0.05~0.30mass%
Kind or aluminium alloy of more than two kinds are constituted.
10. aluminium, Al alloy clad material as claimed in claim 7 or 8, it is characterised in that:
Solder and covering of the covering on the surface of the non-core material side of the intermediate layer material are on another surface of the core material
On solder by also containing selected from Zn:0.5~8.0mass%, Cu:0.05~1.50mass%, Mn:0.05~
2.00mass%, Ti:0.05~0.30mass%, Zr:0.05~0.30mass%, Cr:0.05~0.30mass% and V:
One kind or two or more aluminium alloy in 0.05~0.30mass% is constituted.
11. aluminium, Al alloy clad material as claimed in claim 7 or 8, it is characterised in that:
Solder and covering of the covering on the surface of the non-core material side of the intermediate layer material are on another surface of the core material
On solder by also containing a kind or 2 kinds in Na:0.001~0.050mass% and Sr:0.001~0.050mass%
Aluminium alloy constitute.
12. a kind of manufacturing method of aluminium, Al alloy clad material is used for the conjunction of aluminium described in any one of manufacturing claims 7~11
Golden clad material, the manufacturing method are characterised by comprising:
Cast respectively the aluminium alloy of the core material, the aluminium alloy of intermediate layer material, covering intermediate layer material non-core material
The process of the aluminium alloy of solder of the aluminium alloy and covering of solder on the surface of side on another surface of core material；
By solder ingot bar on the surface of the non-core material side of intermediate layer material of casting obtained intermediate layer material ingot bar, covering and
Solder ingot bar of the covering on another surface of core material is hot-rolled down to the hot-rolled process of specific thickness respectively；
The intermediate layer material of specific thickness is made in a surface top covering of core material ingot bar, in the non-core of the intermediate layer material
The solder of specific thickness has been made in the surface top covering of material side, and regulation thickness has been made in another surface top covering of core material ingot bar
The covering process of clad material is made in the solder of degree；
The covering hot-rolled process of hot rolling is carried out to clad material；
The cold rolling process of cold rolling is carried out to the clad material Jing Guo covering hot rolling；With
When one of after the midway of cold rolling process and cold rolling process or both, anneal to clad material 1 time or more
Annealing operation,
In the covering hot-rolled process, rolling start temperature is 400~520 DEG C, is 200~400 by the temperature of clad material
The reduction ratio of DEG C 1 passage of period be limited in 5 times in 30% or more rolling pass hereinafter,
In the annealing operation, clad material is kept for 1~10 hour with 200~560 DEG C.
13. a kind of heat exchanger, it is characterised in that:
It is the heat exchanger for having used aluminium, Al alloy clad material described in any one of Claims 1 to 5 and 7~11.
14. a kind of manufacturing method of heat exchanger is used for heat exchanger described in manufacturing claims 13, the manufacturing method
It is characterized in that:
In inactive gas atmosphere, aluminum alloy materials are brazed using solder flux.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014-001220 | 2014-01-07 | ||
| JP2014001220 | 2014-01-07 | ||
| PCT/JP2014/006306 WO2015104760A1 (en) | 2014-01-07 | 2014-12-17 | Aluminium-alloy clad material and production method therefor, and heat exchanger using said aluminium-alloy clad material and production method therefor |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105745343A CN105745343A (en) | 2016-07-06 |
| CN105745343B true CN105745343B (en) | 2019-05-03 |
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| CN201480062580.5A Active CN105745343B (en) | 2014-01-07 | 2014-12-17 | Aluminium, Al alloy clad material and its manufacturing method and the heat exchanger and its manufacturing method for using the aluminium, Al alloy clad material |
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|---|---|
| US (1) | US9976201B2 (en) |
| JP (1) | JP6452626B2 (en) |
| CN (1) | CN105745343B (en) |
| DE (1) | DE112014006121T5 (en) |
| PT (1) | PT2015104760B (en) |
| WO (1) | WO2015104760A1 (en) |
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| JP5844212B2 (en) * | 2012-05-07 | 2016-01-13 | 株式会社Uacj | Aluminum alloy brazing sheet |
| JP6047304B2 (en) * | 2012-05-11 | 2016-12-21 | 株式会社Uacj | High strength aluminum alloy brazing sheet and method for producing the same |
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2014
- 2014-12-17 CN CN201480062580.5A patent/CN105745343B/en active Active
- 2014-12-17 WO PCT/JP2014/006306 patent/WO2015104760A1/en active Application Filing
- 2014-12-17 PT PT2014006306A patent/PT2015104760B/en active IP Right Grant
- 2014-12-17 US US15/108,566 patent/US9976201B2/en not_active Expired - Fee Related
- 2014-12-17 JP JP2015556636A patent/JP6452626B2/en active Active
- 2014-12-17 DE DE112014006121.2T patent/DE112014006121T5/en not_active Withdrawn
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1826220A (en) * | 2003-07-18 | 2006-08-30 | 克里斯铝轧制品有限公司 | High strength aluminium alloy brazing sheet |
Also Published As
| Publication number | Publication date |
|---|---|
| US9976201B2 (en) | 2018-05-22 |
| CN105745343A (en) | 2016-07-06 |
| PT2015104760B (en) | 2019-12-12 |
| DE112014006121T5 (en) | 2016-09-22 |
| JP6452626B2 (en) | 2019-01-16 |
| JPWO2015104760A1 (en) | 2017-03-23 |
| WO2015104760A1 (en) | 2015-07-16 |
| US20160319401A1 (en) | 2016-11-03 |
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